CN109261971A - One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity - Google Patents
One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity Download PDFInfo
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- CN109261971A CN109261971A CN201810997544.8A CN201810997544A CN109261971A CN 109261971 A CN109261971 A CN 109261971A CN 201810997544 A CN201810997544 A CN 201810997544A CN 109261971 A CN109261971 A CN 109261971A
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- 239000000843 powder Substances 0.000 title claims abstract description 63
- 238000000498 ball milling Methods 0.000 title claims abstract description 46
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 38
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 38
- 239000002131 composite material Substances 0.000 title claims abstract description 37
- 238000000034 method Methods 0.000 title claims abstract description 25
- 239000011159 matrix material Substances 0.000 title claims abstract description 16
- 229910018563 CuAl2 Inorganic materials 0.000 title claims abstract description 14
- 238000002156 mixing Methods 0.000 title claims abstract description 14
- QPLDLSVMHZLSFG-UHFFFAOYSA-N Copper oxide Chemical compound [Cu]=O QPLDLSVMHZLSFG-UHFFFAOYSA-N 0.000 claims abstract description 35
- 239000011812 mixed powder Substances 0.000 claims abstract description 28
- 239000004411 aluminium Substances 0.000 claims abstract description 22
- 229960004643 cupric oxide Drugs 0.000 claims abstract description 18
- 238000000713 high-energy ball milling Methods 0.000 claims abstract description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 14
- 239000000463 material Substances 0.000 claims abstract description 14
- 238000011282 treatment Methods 0.000 claims abstract description 12
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052593 corundum Inorganic materials 0.000 claims abstract description 11
- 229910001845 yogo sapphire Inorganic materials 0.000 claims abstract description 11
- 229910052786 argon Inorganic materials 0.000 claims abstract description 7
- 239000007789 gas Substances 0.000 claims abstract description 7
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 6
- 238000000227 grinding Methods 0.000 claims abstract description 6
- 238000000465 moulding Methods 0.000 claims abstract description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 4
- 239000010439 graphite Substances 0.000 claims abstract description 4
- 241000208340 Araliaceae Species 0.000 claims 1
- 235000005035 Panax pseudoginseng ssp. pseudoginseng Nutrition 0.000 claims 1
- 235000003140 Panax quinquefolius Nutrition 0.000 claims 1
- 235000008434 ginseng Nutrition 0.000 claims 1
- 238000005245 sintering Methods 0.000 description 16
- 239000010935 stainless steel Substances 0.000 description 6
- 229910001220 stainless steel Inorganic materials 0.000 description 6
- 238000002360 preparation method Methods 0.000 description 4
- 235000021355 Stearic acid Nutrition 0.000 description 3
- 239000011324 bead Substances 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 238000011065 in-situ storage Methods 0.000 description 3
- QIQXTHQIDYTFRH-UHFFFAOYSA-N octadecanoic acid Chemical compound CCCCCCCCCCCCCCCCCC(O)=O QIQXTHQIDYTFRH-UHFFFAOYSA-N 0.000 description 3
- OQCDKBAXFALNLD-UHFFFAOYSA-N octadecanoic acid Natural products CCCCCCCC(C)CCCCCCCCC(O)=O OQCDKBAXFALNLD-UHFFFAOYSA-N 0.000 description 3
- 238000004886 process control Methods 0.000 description 3
- 239000008117 stearic acid Substances 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000005303 weighing Methods 0.000 description 3
- 229910018565 CuAl Inorganic materials 0.000 description 2
- 238000009833 condensation Methods 0.000 description 2
- 230000005494 condensation Effects 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 238000007731 hot pressing Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 239000005751 Copper oxide Substances 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 229910000431 copper oxide Inorganic materials 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 210000001519 tissue Anatomy 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/23—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces involving a self-propagating high-temperature synthesis or reaction sintering step
-
- B22F1/0003—
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
- C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The present invention relates to one kind for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity, including the following steps: (1) prepare mixed-powder: according to cupric oxide powder: aluminium powder or Al alloy powder mass ratio are to weigh mixed-powder less than 10%；(2) low energy ball-milling treatment is carried out to mixed-powder: configured mixed-powder is fitted into spheroidal graphite tank, low energy ball milling is carried out to mixed-powder under protection of argon gas, ball milling parameter: ratio of grinding media to material 5:1~15:1, revolving speed 200r/min, Ball-milling Time 2-4 hours；(3) high-energy ball milling processing being carried out to mixed-powder: the powder after low speed in short-term ball milling is subjected to high-energy ball milling processing, high-energy ball milling treatment process is revolving speed 400r/min, Ball-milling Time 2-4 hours；(4) sinter molding.
Description
Technical field
Nanometer CuAl is improved using improved ball milling blending processes of powders the present invention relates to a kind of2/Al2O3Enhance aluminum-base composite
The method of material homogeneity belongs to metal-base composites preparation technical field.
Background technique
Aluminum matrix composite specific strength with higher and specific modulus, thus application field is very extensive.In recent years, section
The worker of grinding is dedicated to by way of powder metallurgy fabricated in situ reinforced phase further to improve the mechanics of aluminum matrix composite
Performance.Among the material system of numerous fabricated in situ aluminum matrix composites, using cupric oxide powder and aluminium powder as raw material, using height
Can ball milling mode can in aluminium (aluminium alloy) matrix fabricated in situ nanometer CuAl2With nanometer Al2O3, to obtain resultant force
Learn the aluminum matrix composite of better performances.
But found during carrying out Mechanics Performance Testing to such composite material, although its tensile strength can achieve
200MPa or more improves 100% compared with fine aluminium.But once composite material enters plastic period in deformation process,
Engineering stress strain curve then can there is a phenomenon where serrated plastic flows.The behavior for generating serrated plastic flow is largely due to again
Caused by condensation material interior tissue is uneven.In the continuous loading procedure of composite material, since reinforced phase intensity is higher than aluminum substrate,
Therefore the reinforced phase of local a direction carries first is broken until reaching its strength degree, constantly carries in reinforced phase
Cheng Zhong shows as the raising of composite material strength on engineering stress strain curve；When it is broken, answered in engineering stress
The steep drop of composite material strength is shown as on varied curve.Two above process constitutes one " sawtooth " in stress-strain diagram
Process.As the reinforced phase of different zones different directions is constantly there is a phenomenon where carrying until fracture, engineering stress strain curve
The phenomenon that showing " serrated plastic flow " on the whole.
In order to further enhance composite material uniformity, make CuAl2/Al2O3Nanometer reinforcing phase can be realized in material internal
The effect uniformly carried can start in terms of following two.First is that being directed to CuAl2This intermetallic compound, can be to burning
Composite material after knot carries out Homogenization Treatments, makes CuAl2The process that back dissolving-is precipitated again is realized, to change CuAl2Compound
Pattern and distribution in material system.Second is that start with from preparation process, make in such a way that ball milling mixes powder original material (aluminium powder,
Cupric oxide powder) realize uniformly mixing, the structural homogenity of composite material is promoted with this.
Summary of the invention
The purpose of the present invention is to provide a kind of improvement CuAl2/Al2O3The speed change ball milling of reinforced aluminum matrix composites mixes powder
Method.This method can be effectively improved CuAl2/Al2O3It is disconnected to improve composite material for the structural homogenity of reinforced aluminum matrix composites
Behavior is split, composite material strength and elongation percentage are further promoted.To achieve the above object, the present invention adds by the following technical programs
To implement.
One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity, packet
Include the following steps:
(1) mixed-powder is prepared
According to cupric oxide powder: aluminium powder or Al alloy powder mass ratio are to weigh mixed-powder less than 10%.
(2) low energy ball-milling treatment is carried out to mixed-powder
Configured mixed-powder is fitted into spheroidal graphite tank, low energy ball milling, ball are carried out to mixed-powder under protection of argon gas
Mill parameter: ratio of grinding media to material 5:1~15:1, revolving speed 200r/min, Ball-milling Time 2-4 hours.
(3) high-energy ball milling processing is carried out to mixed-powder
Powder after low speed in short-term ball milling is subjected to high-energy ball milling processing, high-energy ball milling treatment process is revolving speed 400r/
Min, Ball-milling Time 2-4 hours.
(4) sinter molding.
Homogenize mixing mechanism: after mixing with aluminium powder thermit reaction can occur at high temperature for cupric oxide powder.If energy
It enough realizes that cupric oxide powder is uniformly mixed with aluminium powder, is then expected to obtain the equally distributed aluminum matrix composite of reinforced phase.Changeup
During mill, increase the dispersibility of cupric oxide powder by low energy ball milling first, and realizes the uniform of cupric oxide powder and aluminium powder
Mixing.In subsequent Process During High Energy Ball Milling, surface is attached with aluminium powder process deformation-broken-cold welding of cupric oxide powder
Cupric oxide powder is wrapped among aluminium powder by process, realizes that cupric oxide powder is uniformly distributed.
Detailed description of the invention
Fig. 1 is original aluminium powder pattern
Fig. 2 is native oxide copper powder pattern
Fig. 3 is that low energy ball milling mixes pattern after powder
Fig. 4 is that high-energy ball milling mixes pattern after powder
Fig. 5 is engineering stress-strain curve of the fine aluminium of hot pressing state composite material and same process preparation.
Specific embodiment
Technology path of the invention is as follows:
(1) mixed-powder is prepared
According to cupric oxide powder: aluminium powder or Al alloy powder mass ratio are to weigh mixed-powder less than 10%, wherein copper oxide
The partial size of powder is 5-10 μm, and the partial size of aluminium powder or Al alloy powder is 30-40 μm.
(2) low energy ball-milling treatment is carried out to mixed-powder
Configured mixed-powder is fitted into spheroidal graphite tank, low energy ball milling, ball are carried out to mixed-powder under protection of argon gas
Mill parameter: ratio of grinding media to material 5:1~15:1, revolving speed 200r/min, Ball-milling Time 2-4 hours.
(3) high-energy ball milling processing is carried out to mixed-powder
Powder after low speed in short-term ball milling is subjected to high-energy ball milling processing, high-energy ball milling treatment process is revolving speed 400r/
Min, Ball-milling Time 2-4 hours.
(4) sinter molding
Powder after speed change ball milling is put into the mold of vacuum hotpressing stove and carries out Thermocompressed sintering and forming.Sintering pressure is
50MPa, sintering temperature are 620 DEG C.The pressure sintering process such as HIP sintering, discharge plasma sintering, cold pressing thermal sintering are equal
It can be used for powder sintered molding.The composite material of preparation can further be promoted multiple by deformation techniques such as subsequent extrusion, rollings
Condensation material mechanical property.
It further illustrates that the present invention, these examples are served only for illustrating the present invention below with reference to example, is not intended to limit the present invention.
Embodiment 1
Weigh the aluminium powder 19g (shown in Fig. 1) that partial size is about 400 mesh, partial size is 5~10 μm of cupric oxide powder 1g (Fig. 2 institute
Show), while weighing the stearic acid that mass fraction is 1% and being used as process control agent, it is placed in 250 milliliters of stainless steel jar mill.
Stainless steel ball 300g (ratio of grinding media to material 15:1) is weighed, wherein big ball and bead number ratio are 1:2.And it is filled with argon gas.Using planet
Formula ball mill carries out low speed ball-milling treatment first, revolving speed 200r/min, and Ball-milling Time 2 hours (shown in Fig. 3).Then carry out
High-energy ball milling processing, revolving speed 400r/min, Ball-milling Time 4h (shown in Fig. 4).Ball milling takes out in vacuum glove box after mixing powder
Mixed-powder uses diameter for the mold of 45mm progress vacuum heating-press sintering, and 620 DEG C of sintering temperature, sintering pressure 50MPa.?
It is 45mm nanometers of CuAl to diameter2/Al2O3Reinforced aluminum matrix composites sample.
It by linear cutter is the style that can be used for stretching by aluminum matrix composite, using universal tensile testing machine
It is stretched, rate of extension 0.5mm/min, obtains the engineering stress strain curve of the composite material (shown in Fig. 5).
Embodiment 2
The aluminium powder 19g that partial size is about 400 mesh is weighed, partial size is 5~10 μm of cupric oxide powder 1g, while weighing quality point
The stearic acid that number is 1% is placed in 250 milliliters of stainless steel jar mill as process control agent.Weigh stainless steel ball 300g (ball
Material is than being 15:1), wherein big ball and bead number ratio are 1:2.And it is filled with argon gas.Low speed is carried out using planetary ball mill first
Ball-milling treatment, revolving speed 200r/min, Ball-milling Time 2 hours.Then carry out high-energy ball milling processing, revolving speed 400r/min, ball
Consume time 2h.Ball milling takes out mixed-powder after mixing powder in vacuum glove box, and diameter is used to carry out Vacuum Heat for the mold of 45mm
Pressure sintering, 620 DEG C of sintering temperature, sintering pressure 50MPa.Obtaining diameter is 45mm nanometers of CuAl2/Al2O3Enhance aluminum-base composite material
Expect sample.
It by linear cutter is the style that can be used for stretching by aluminum matrix composite, using universal tensile testing machine
It is stretched, rate of extension 0.5mm/min, obtains the engineering stress strain curve of the composite material.
Embodiment 3
The aluminium powder 19g that partial size is about 400 mesh is weighed, partial size is 5~10 μm of cupric oxide powder 1g, while weighing quality point
The stearic acid that number is 1% is placed in 250 milliliters of stainless steel jar mill as process control agent.Weigh stainless steel ball 300g (ball
Material is than being 15:1), wherein big ball and bead number ratio are 1:2.And it is filled with argon gas.Low speed is carried out using planetary ball mill first
Ball-milling treatment, revolving speed 200r/min, Ball-milling Time 2 hours.Then carry out high-energy ball milling processing, revolving speed 400r/min, ball
Consume time 2h.Ball milling takes out mixed-powder after mixing powder in vacuum glove box, and diameter is used to carry out Vacuum Heat for the mold of 20mm
Pressure sintering, 620 DEG C of sintering temperature, sintering pressure 50MPa.Obtaining diameter is 20mm nanometers of CuAl2/Al2O3Enhance aluminum-base composite material
Expect sample.
Sintered composite material is subjected to hot extrusion, squeezes 550 DEG C of temperature, extrusion ratio 16:1.Obtain diameter
For the extruded bars of 5mm.It is the rodlike stretching style of dog bone that extruded bars, which are passed through linear cutter, using universal tensile testing machine
It is stretched, rate of extension 0.5mm/min, obtains the engineering stress strain curve of the composite material.
The present invention increases the uniformity of mixed-powder in such a way that speed change ball milling mixes powder by low energy ball milling first, then
High-energy ball milling is carried out, promotes the plastic deformation of aluminium powder, and then will be attached in the cupric oxide powder package to aluminium powder on aluminium powder surface
Portion.By the Style of mixing powder of speed change ball milling, it can be effectively improved the uniformity of composite material, advanced optimize the power of composite material
Learn performance.
Claims (1)
1. one kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity, including
The following steps:
(1) mixed-powder is prepared
According to cupric oxide powder: aluminium powder or Al alloy powder mass ratio are to weigh mixed-powder less than 10%；
(2) low energy ball-milling treatment is carried out to mixed-powder
Configured mixed-powder is fitted into spheroidal graphite tank, low energy ball milling, ball milling ginseng are carried out to mixed-powder under protection of argon gas
Number: ratio of grinding media to material 5:1~15:1, revolving speed 200r/min, Ball-milling Time 2-4 hours.
(3) high-energy ball milling processing is carried out to mixed-powder
Powder after low speed in short-term ball milling is subjected to high-energy ball milling processing, high-energy ball milling treatment process is revolving speed 400r/min, ball
Time consuming 2-4 hours；
(4) sinter molding.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810997544.8A CN109261971A (en) | 2018-08-29 | 2018-08-29 | One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810997544.8A CN109261971A (en) | 2018-08-29 | 2018-08-29 | One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN109261971A true CN109261971A (en) | 2019-01-25 |
Family
ID=65155057
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810997544.8A Pending CN109261971A (en) | 2018-08-29 | 2018-08-29 | One kind is for improving nanometer CuAl2/Al2O3The speed change ball milling powder mixing method of reinforced aluminum matrix composites uniformity |
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| Country | Link |
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| CN (1) | CN109261971A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112626367A (en) * | 2021-01-06 | 2021-04-09 | 山东省科学院新材料研究所 | Preparation method of nano alumina particle reinforced aluminum-copper alloy composite material |
| CN113174508A (en) * | 2021-03-09 | 2021-07-27 | 江苏大学 | In-situ Al2O3Preparation method of particle reinforced aluminum matrix composite |
| CN115229197A (en) * | 2022-07-29 | 2022-10-25 | 西北工业大学 | Method for uniformly dispersing discontinuous reinforcement in high-strength aluminum alloy |
| CN116411199A (en) * | 2023-06-12 | 2023-07-11 | 内蒙古工业大学 | Al 2 O 3 Particles and Al 2 Cu jointly reinforced aluminum-based composite material and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050069449A1 (en) * | 2003-09-26 | 2005-03-31 | Jackson Melvin Robert | High-temperature composite articles and associated methods of manufacture |
| CN101376171A (en) * | 2008-10-09 | 2009-03-04 | 上海交通大学 | Method for preparing reinforced aluminum-base compound material with locally distributed granule |
| CN101838755A (en) * | 2010-06-13 | 2010-09-22 | 上海交通大学 | Local particle reinforced metal matrix composite material and preparation method thereof |
| CN106363185A (en) * | 2016-08-26 | 2017-02-01 | 上海交通大学 | Powder metallurgy preparation method of nanophase/metal composite powder and block material thereof |
-
2018
- 2018-08-29 CN CN201810997544.8A patent/CN109261971A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050069449A1 (en) * | 2003-09-26 | 2005-03-31 | Jackson Melvin Robert | High-temperature composite articles and associated methods of manufacture |
| CN101376171A (en) * | 2008-10-09 | 2009-03-04 | 上海交通大学 | Method for preparing reinforced aluminum-base compound material with locally distributed granule |
| CN101838755A (en) * | 2010-06-13 | 2010-09-22 | 上海交通大学 | Local particle reinforced metal matrix composite material and preparation method thereof |
| CN106363185A (en) * | 2016-08-26 | 2017-02-01 | 上海交通大学 | Powder metallurgy preparation method of nanophase/metal composite powder and block material thereof |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112626367A (en) * | 2021-01-06 | 2021-04-09 | 山东省科学院新材料研究所 | Preparation method of nano alumina particle reinforced aluminum-copper alloy composite material |
| CN112626367B (en) * | 2021-01-06 | 2022-01-11 | 山东省科学院新材料研究所 | Preparation method of nano alumina particle reinforced aluminum-copper alloy composite material |
| CN113174508A (en) * | 2021-03-09 | 2021-07-27 | 江苏大学 | In-situ Al2O3Preparation method of particle reinforced aluminum matrix composite |
| CN115229197A (en) * | 2022-07-29 | 2022-10-25 | 西北工业大学 | Method for uniformly dispersing discontinuous reinforcement in high-strength aluminum alloy |
| CN115229197B (en) * | 2022-07-29 | 2023-07-21 | 西北工业大学 | Method for uniformly dispersing discontinuous reinforcement in high-strength aluminum alloy |
| CN116411199A (en) * | 2023-06-12 | 2023-07-11 | 内蒙古工业大学 | Al 2 O 3 Particles and Al 2 Cu jointly reinforced aluminum-based composite material and preparation method thereof |
| CN116411199B (en) * | 2023-06-12 | 2023-08-04 | 内蒙古工业大学 | Al 2 O 3 Particles and Al 2 Cu jointly reinforced aluminum-based composite material and preparation method thereof |
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Application publication date: 20190125 |